Persistent-Mode MRI Magnet Fabricated From Reacted, Monofilamentary MgB2 Wires And Joints

ABSTRACT

A superconducting magnet and method for making a superconducting magnet are presented. The superconducting magnet is made by forming a coil from windings of a first wire comprising a reacted MgB 2  monofilament, filling a cavity of a stainless steel billet with a Mg+B powder. Monofilament ends of the first wire and a similar second wire are sheared at an acute angle and inserted into the billet. A copper plug configured to partially fill the billet cavity is inserted into the billet cavity. A portion of the billet adjacent to the plug and the wires is sealed with a ceramic paste.

CROSS-REFERENCE TO RELATED APPLICATION

This application is a divisional of and claims the benefit of U.S.patent application Ser. No. 14/330,689, filed Jul. 14, 2014, entitled“Persistent-Mode MRI Magnet Fabricated From Reacted, MonofilamentaryMgB2 Wires And Joints,” which claims the benefit of U.S. ProvisionalPatent Application Ser. No. 61/846,067, filed Jul. 14, 2013, entitledPersistent-mode MM magnet fabricated from reacted, monofilamentary MgB2wires, both of which are incorporated by reference herein in itsentirety.

GOVERNMENT LICENSE RIGHTS

This invention was made with government support under Grant No. EB002887awarded by the National Institutes of Health. The government has certainrights in the invention.

FIELD OF THE INVENTION

The present invention relates to superconducting materials, and moreparticularly, is related to superconducting magnets.

BACKGROUND OF THE INVENTION

Magnetic resonance imaging (MRI) magnets are important for qualityhealth care, for example, in early detection and efficient treatment ofdiseases or injuries. An MM magnet typically includes a coil ofsuperconducting wire, a wire joint, and a persistent current switch(PCS).

PCSs are provided on many magnets to increase their temporal stabilityover long periods of time or to reduce the rate of helium boil-offassociated with continually supplying current to the magnet usingcurrent leads. A PCS generally includes a short section ofsuperconducting wire connected across the input terminals of a magnetand an integral heater used to drive the wire into the resistive, normalstate. When the heater is turned on and the wire is resistive, a voltageis established across the terminals of the magnet and the magnet can beenergized. Once energized, the heater may be turned off when the wirebecomes superconducting and further changes in the magnet current cannotbe made. In this persistent mode of operation, the external power supplycan be turned off to reduce the heat input to the helium bath and thecurrent will continue to circulate through the magnet and the PCS.

Existing MRI magnets are typically made from multifilamentniobium-titanium (NbTi) wires. For these magnets, it is generallynecessary to use multifilament superconducting wires to prevent anadverse condition known as flux-jumping, which makes it impossible tooperate the magnet at full field. It is generally agreed, thatmonofilament NbTi wire is unsuitable for magnets because of fluxjumping. Flux jumping depends on several characteristics of the wire andassociated magnet. These characteristics include the filament diameterand also the operating temperature of the magnet. Existing magnetsoperate in liquid helium temperature (4K) and thereby require very smallfilaments, thus, the multifilament wires. As a result, these MRI magnetsare very costly to buy and operate.

Most MRI magnets are operated in persistent mode. Therefore asuperconducting joint technique is needed to splice MRI magnet wires tothe MM magnet, for example, a 0.5 T whole-body MRI magnet. However,splicing of conventional NbTi monofilament wires to an MM magnet mayresult in reliability issues, for example, flux jumping as describedabove.

While it is fairly easy to make a persistent, superconducting jointbetween two unreacted ceramic wires, as ceramic powder reaches asemi-liquid state at the heat treatment at reasonably low temperatures,reacted wires are hard ceramics, making them much more difficult tojoin.

Reacted magnets can be made using a reacted, persistent wire joint;however, this approach is unattractive for two main reasons. First, inorder to form the reacted joint, the entire magnet needs to beheat-treated in a furnace, or oven, after winding. Therefore, all of themagnet materials, including the wire insulation, winding mandrel, etcetera, need to be able to withstand high heat treatment temperatures of˜650 C. Second, if the unreacted wire joint does not work properly,there is no chance to re-make the joint, as the magnet wire is nowreacted, thereby resulting in the whole magnet being unusable, makingthis an unacceptable risk for commercial manufacturing of MRI magnets.Therefore, there is a need in the industry to address at least some ofthe abovementioned shortcomings.

SUMMARY OF THE INVENTION

Embodiments of the present invention provide a persistent-mode Millmagnet fabricated from reacted, monofilamentary MgB₂ wires and joints.Briefly described, the present invention is directed to a method formaking a superconducting magnet. The superconducting magnet is made byforming a coil from windings of a first wire comprising a reacted MgB₂monofilament, filling a cavity of a stainless steel billet with an Mg+Bpowder. Monofilament ends of the first wire and a similar second wireare sheared at an acute angle and inserted into the billet. A copperplug configured to partially fill the billet cavity is inserted into thebillet cavity. A portion of the billet adjacent to the plug and thewires are sealed with a ceramic paste.

Other systems, devices, methods and features of the present inventionwill be or become apparent to one having ordinary skill in the art uponexamining the following drawings and detailed description. It isintended that all such additional systems, methods, and features beincluded in this description, be within the scope of the presentinvention and protected by the accompanying claims.

BRIEF DESCRIPTION OF THE DRAWINGS

The accompanying drawings are included to provide a furtherunderstanding of the invention, and are incorporated in and constitute apart of this specification. The drawings illustrate embodiments of theinvention and, together with the description, serve to explain theprincipals of the invention.

FIG. 1A is a schematic diagram of a wire joint under the firstembodiment in an exploded view.

FIG. 1B is a schematic diagram of the wire joint under the firstembodiment in an assembled perspective view.

FIG. 1C is a schematic diagram of the wire joint under the firstembodiment from a side cutaway view.

FIG. 1D is a schematic diagram of the wire joint under the firstembodiment from a top view.

FIG. 2 is a flowchart showing an exemplary method for forming the wirejoint of FIGS. 1A-1D.

FIG. 3 is a chart summarizing critical currents under the firstembodiment, measured at 10 K, 15 K, and 20 K in self-field, of 12angle-cut MgB₂ joints.

FIG. 4 is a plot of resistance vs. temperature profile of an MgB₂ jointof FIG. 3.

FIG. 5 is a graph plotting magnetization vs. field trace of a bundle of12 short samples of monofilament MgB₂.

FIG. 6 is a graph plotting magnetization vs. field trace of a bundle ofshort samples of prior art monofilament NbTi.

FIG. 7 is a graph plotting voltage vs. current curve of the MgB₂ testcoil measured at 15 K and in self-field at a ramping rate of 1 A/s.

FIG. 8 is a graph plotting voltage vs. current curve of the MgB₂ testcoil measured at 15 K and in self-field at a ramping rate of 5 A/s.

FIG. 9 is schematic diagram of an MM magnet under a second exemplaryembodiment.

FIG. 10 is schematic diagram of an MM magnet system under an alternativeexemplary embodiment.

DETAILED DESCRIPTION

Reference will now be made in detail to embodiments of the presentinvention, examples of which are illustrated in the accompanyingdrawings. Wherever possible, the same reference numbers are used in thedrawings and the description to refer to the same or like parts. As usedwithin this disclosure, “reacted” refers to a ceramic material that hasbeen solidified, for example, by heating a ceramic powder.

As noted previously, prior art MRI magnets were generally formed ofmultifilament NbTi wire. As noted above, NbTi wire exhibits flux jumpingbehavior, necessitating multi-filament wires. Superconducting NbTi wiresmust be cooled by liquid helium. Further, previous methods of joiningreacted monofilament wires were problematic, making MRI magnets usingsuch wires unfeasible. Embodiments of the present invention include anMRI magnet made from reacted, monofilament reacted magnesium diboride(MgB₂) wires, including a persistent superconducting joint. Thecombination of this reacted joint with the monofilament MgB₂ magnetmakes this novel technology valuable.

Under a first exemplary embodiment, a joint is formed by splicing tworeacted MgB₂ monofilament superconducting wires. For example, such wiresare manufactured by HyperTech, consisting, from innermost to outermost,of an MgB₂ core of 0.4 mm in diameter, a layer of niobium, a layer ofcopper, and a layer of Monel. For example, an overall diameter of thewire may be 0.8 mm bare. In applying the splicing technique (describedbelow), the joining may occur at a sintering temperature of 700° C. for90 minutes, a combination of temperature and duration required to reactthe winding itself. This is important because an MM magnet of the secondembodiment (described below) applies a wind-and-react procedure. The MRImagnet is wound with MgB₂ in a fashion similar to winding with NbTiwire, as is familiar to persons having ordinary skill in the art, sothis disclosure instead discusses the differences involved in using MgB₂wire for an MRI magnet, and in particular, an MgB₂ wire joint.

FIG. 2 is a flowchart showing a modified joining fabrication process ofa joint 100 between two reacted MgB₂ wires 130 is shown in FIGS. 1A-1D.It should be noted that any process descriptions or blocks in flowchartsshould be understood as representing modules, segments, portions ofcode, or steps that include one or more instructions for implementingspecific logical functions in the process, and alternativeimplementations are included within the scope of the present inventionin which functions may be executed out of order from that shown ordiscussed, including substantially concurrently or in reverse order,depending on the functionality involved, as would be understood by thosereasonably skilled in the art of the present invention.

As shown by block 210 a cladding of the wires 130 surrounding themonofilaments 135, for example, copper and Monel cladding, is etched,for example, with nitric acid. The filaments 135 may be preferablysheared at an acute angle for each wire 130, as shown by block 220. Forexample, the filaments 135 may be sheared at an angle of 45 degrees orless with respect to a center axis of the wire. A more acute angleprovides a larger splicing surface, better enabling conduction throughthe joint. In general, the more acute the wire cutting angle, thebetter, although a joint 100 may function correctly even if the wires130 are cut at a 90 degree angle with respect to a center axis of thewire 130. Ideally, a cut could be made nearly parallel to the axis ofthe wire (splitting the wire in half), although this may not bepractical with a shear.

A billet 110, is formed from a material able to withstand and/or exertappropriate pressure on the contents of a cavity 115 within the billet110. For example, the billet 110 may be formed of stainless steel. Othermaterials for the billet 110 may be used, provided the materials have amelting point greater than a heat treatment temperature of 700 Celsius,and a Young's modulus of greater than 60 MPa. The cavity 115 is filledwith a ceramic powder 150, for example, pre-mixed Mg+B powder havinga1:2 ration of Mg to B. However, other ratios are possible, for example,a more magnesium-rich ratio of Mg:B>1:2. In general, a ratio of at least1 part Mg to 2 parts B is acceptable, as the magnesium vaporizes.

A plug 120, for example, a copper plug, is inserted into the billetcavity 115 without applying pressure to the ceramic powder 150, as shownby block 230. Other materials for the plug 120 may be used, provided thematerials have a melting point greater than a heat treatment temperatureof 700 Celsius, and a Young's modulus of greater than 60 MPa. The twowires 130 are inserted into the billet cavity 115 in an opening betweena flat surface 125 of the plug 120 and the billet 110, aligning thewires 130 so that the angle-cut surfaces of the filaments 135 face eachother within the cavity 115, as shown by block 240. The plug 120 ispressed into the billet cavity 115 to partially seal the top of thebillet 110, as shown by block 250.

Pressure is applied to the top of the plug 120 downward into the billetcavity 115 in a direction parallel to a center axis of the wires 130, sothat the pressure is less likely to damage the sheared monofilaments 135than pressure applied in a direction traversing the center axis of thewires 130. For example, pressure levels on the order of 1 GPa (higherthan the yield strength of stainless steel) may be applied to press theplug 110 into the billet cavity 115. If other high density ceramics orunreacted wires are used, higher pressures may be used, for example,stresses in the 2-5 GPa range, which may need additional tooling to keepthe billet in isostatic compression, so that no deformation occurs. Ifexcessive pressure is used, the billet 120 or the plug 110 may bedamaged. If insufficient pressure is applied, the joint 100 may notfunction correctly. The top of the billet 110 is sealed, for example,using ceramic paste 140, completely sealing the top of the billet cavity115, as shown by block 260.

The three main benefits to this new process are that: (1) the relativelyfragile sheared filaments 135 are aligned with the pressing direction ofthe plug 120, reducing the possibility of breaking the filaments 135,(2) the acute angle cut of the filaments 135 maximizes the joint surfacearea, resulting in higher joint critical currents and betterreproducibility, and (3) this method implements simpler parts andminimizes handling and assembly time when compared with the prior art.

Compared with the prior art, key differences in forming a reacted joint100 under the first embodiment may include one or more of: (1) higherpowder compaction pressure; (2) a billet able to enable these higherpacking pressures; (3) a change in the tooling required to apply thesehigh pressures; and (4) changes in the heat treatment profile, includingtime and/or temperature. For example, while heat treatment should exceedthe melting temperature of magnesium (650 C), otherwise there is noupper bound to either the time or temperature for the heat treatmentprofile.

In alternative embodiments, the copper steel (or stainless steel) plug120 may incorporate a center hole through which the wires 130 areinserted. A compacting rod used to press the plug 120 into the billetcavity 115 may similarly have a center hole to accommodate the ends ofthe wires 130. The compacting rod may accommodate a tight fit to theoutside of the billet 110. In this manner, force may be appliedsymmetrically down the center axis of the billet 110, preventing anybending which could snap the wires 130. Such a compacting rod mayprovide compressing the billet 110 to higher loads upwards of 10,000lbs. in order to exceed 1 GPa powder packing pressure. At these highpressures, it may be difficult to extract the billet 110 from thecompacting rod. Other compressing means are also possible, for example,but not limited to including a two part mold for this process.

As noted previously, while joints for unreacted wire are relativelysimple, constructing an MRI magnet from unreacted wire is problematic,as each of the components of the magnet would have to be subject to theheating of the reacting process. Therefore, the former or bobbin of amagnet coil would need to be made of a material to withstand this heat.In contrast, a reacted wire magnet may be wound on a non-metallic,lightweight former, such as G-10 or “Garolite,” or similar composites,which are commonly used in MRI magnets today.

FIG. 3 shows a summary of superconducting joint results of ten samplemonofilament MgB₂ wires, measured at 10 K, 15 K, and 20 K in self-field,of 12 angle-cut MgB₂ joints. Most samples had critical currents higherthan 100 A, even at 20 K. 400 A was the limit of the power supply.Critical currents were measured by the four-probe method familiar topersons having ordinary skill in the art. Since the MgB₂ filament issurrounded by niobium, the only part exposed to the Mg+B mixture ingotin a joint 100 (FIG. 1B) is an end tip of the wire filament 135 (FIG.1B) of small contact area. Therefore, in the first embodiment, eachfilament 135 (FIG. 1B) is cut at an acute angle to enlarge this contactarea significantly. FIG. 3 data shows that all the joints haveacceptable (>100 A) critical currents. The best joints have criticalcurrents well above 100 A, e.g., sample #5 with 270 A even at 20 K,which will suffice for use in a 0.5 T whole-body Mill magnet operatingnominally at 10-15 K.

FIG. 4 is a plot of a resistance vs. temperature profile of one of theMgB₂ joints of FIG. 3. The critical temperature was determined bymeasuring the joint resistance during cool-down. The data are plotted inFIG. 4, showing the onset of the superconducting transition at about 36K. However, the whole joint is not superconducting above about 32 K.This rather broad transition observed in the joint 100 (FIG. 1B) may bedue to a slight difference in composition of powders used in the twowires and in the ingot. The steeper section may represent the transitionof wire, while the gradual section may represent the transition of theingot in the joint.

With a successful splicing technique for monofilament MgB₂ wire, an Millmagnet with monofilament MgB₂ wire becomes feasible. Note that it isgenerally agreed, because of flux jumping, that monofilament NbTi wireis unsuitable for magnets. However, theoretically flux jumping isunlikely to happen in MgB₂ wire at 15 K, even if the monofilament is 0.4mm in diameter. The absence of flux jumping in such monofilament MgB₂wire was verified by a series of experiments with short MgB₂ samples andMgB₂ test coils, described below.

Short samples of MgB₂ were cut from the same spool used to make testjoints. The joints were heat treated in the same temperature vs. timeprofile used for the joints and the test coils, i.e., a temperature of700° C. for 90 minutes. A bundle of 12 reacted samples was inserted intothe cold bore (6.4 mm in diameter) of a miniature NbTi magnet. With theNbTi magnet sweeping at a constant rate of 0.5 T/s, the samplemagnetization was measured using a small search coil. Besides MgB₂, abundle of monofilament NbTi short samples, of the similar filament (0.4mm) and overall size, was also tested as a reference. Since NbTi magnetwas employed as the background magnet, these tests were performed at 4.2K only.

FIG. 5 shows a magnetization vs. field trace of the monofilament MgB₂bundle. The trace is generally smooth, except the zero-field dips inmagnetization: each small dip is likely caused by a partial flux jump.

FIG. 6 shows a magnetization vs. field trace of the monofilament NbTibundle. Four in-field dips in magnetization trace indicate partial fluxjumps. The zero-field dips are also more pronounced than those of themonofilament MgB₂ bundle.

In order to further demonstrate that the absence of full flux jumpingobserved in short monofilament MgB₂ wires still holds in coils, a testcoil was built, wound with 100-m long of the same monofilament MgB₂wire. The wire, S-glass insulated, has an overall diameter of 1 mm.

The coil, at 15 K and in self-field, was first charged at a ramping rateof 1 A/s until it quenched at 160 A, which was its critical currentpredicted by short sample tests. A measured voltage vs. current curve isshown in FIG. 7, displaying many voltage spikes. Each voltage spike maybe caused by a flux jump or a mechanical disturbance incident, as thetest coil was not epoxy-impregnated, a standard procedure in NbTimagnets to minimize the mechanical disturbances. As expected, none ofthese voltage spike incidents quenched the test coil.

To further test the coil stability, the coil was charged at a higherramping rate of 5 A/s. As shown by FIG. 8, the spikes are obviouslystronger. But, still, they did not quench the coil even at 90% of thecoil's critical current. The procedure was repeated several times, andevery time the coil was charged up to 90% of its critical currentwithout quench. Therefore this monofilament MgB₂ coil, despite evidencesof either flux motion, mechanical disturbance, or both, was operatedabsolutely quench free.

A second embodiment of the present invention is an MRI magnet 900 formedwith a persistent-mode monofilament MgB₂ coil 910, as shown by FIG. 9.After the monofilament MgB₂ test coil was operated quench free, thepersistent-mode monofilament MgB₂ coil 910 was designed, fabricated, andtested. The coil 910 may be formed by winding multiple windings ofreacted MgB₂ wires 130. The coil 910 may be equipped with a PCS 920 andterminated by a superconducting joint 100, for example, as describedabove under the first embodiment. The coil 910 may be wound, forexample, with 50-m long monofilament MgB₂ wire, as per the testsdescribed above. The wire 130 may be insulated by S-glass. Thecalculated center field may be, for example, 0.84 T at 100 A current, atwhich the maximum field in the winding is 0.94 T. The joint 100 may beplaced at the upper edge of the coil, in which the maximum field is 0.35T at 100 A. The PCS may contain the same wire of 1 m long, having 2 mΩopen resistance.

After the coil was wound and heat treated, it was placed in a copper can(not shown), which is housed in an aluminum chamber (not shown). The canprovided an isothermal environment for the coil. A heater (not shown)was wound around the can to heat it up above 4.2 K during the tests. Thecopper can was then placed in the aluminum chamber. The space in betweenthe two enclosures was filled with Styrofoam. The aluminum chamber wasimmersed in liquid helium during tests, with the heater controlling thetemperature of copper can in the range of 4.2 K-15 K.

In the beginning of the test, the PCS 920 was opened, and the coil at 10K was charged by an external power supply at 0.5 A/s up to 100 A. Sincethe time constant of the coil 910 is calculated to be 2 s, a few secondsat 100 A elapsed before closing the PCS, and the external power supplywas then brought to zero.

During charging sequence the field at the center of the coil 910increased linearly with current. The charging behavior indicates that2-mΩ open-resistance of the PCS 920 is large enough for this 3.2-mHcoil, allowing only negligible current through the PCS 920. A measuredfield of 0.83 T at the center matched the calculation, with calculatedfields of 0.94 T (maximum in the winding) and 0.35 T (at joint site).The coil 920 was warmed up from 10 K to 15 K at ˜0.2 K/min and kept at15 K over a period of 2500 s. Limited by measurement resolution, one canonly determine a relative field decay of less than 10-4 over a testperiod of ˜2500 s. This means that the time constant is longer than2.5×10⁷ s, with a computed total circuit resistance of less than1.3×10¹⁰Ω.

MgB₂ has a critical temperature of 39 K, enabling MgB₂ magnets under thesecond embodiment to operate above 4.2 K, the nominal temperature ofmost NbTi MRI magnets. Operation above 4.2 K may reduce the complexityand cost of MRI units. The simple chemical composition of MgB₂ makes themanufacturing of km-long wires possible.

MgB₂ magnets under the second embodiment may be operated above 10 K, atwhich temperature the filament diameter can be on the order of ˜1 mmwithout causing flux-jumping. It has been demonstrated that MgB₂ wireswith 0.8 mm diameter (and 0.4 mm internal filament diameter) can indeedbe made without flux jumping. The present invention is not limited tosuch measurements. Furthermore, it is significantly easier to make asuperconducting joint between two monofilament wires, as opposed tojoining multifilament wires.

In an alternative embodiment, shown in FIG. 10, one or moresuperconducting joints 100 in a magnet system 1000 may be located in ajoint box 1010. The joint box 1010 may be used to heat or cool thejoint(s) 100, as may be needed for a particular magnet system 1000. Forexample, the joints 100 may all be heat treated simultaneously in alocalized furnace 1020 which surrounds the joint box 1010. Additionally,the joint box 1010 may be cooled to a lower temperature (minimum valueof 1.8 K, corresponding to superfluid helium) than a temperature of themain magnet 910 in order to improve performance of the joint(s) 100. Inthis manner, it is possible to use the superconducting properties of theniobium coating on the MgB2 filament to achieve the joint 100superconductivity. For example, the superconducting path may be from onereacted MgB2 filament, thru the niobium barrier, thru the reacted powderin the joint billet, thru the second niobium barrier and into the secondMgB2 filament. The main magnet 910 may still operate at 10 K, while thejoint box 1010 operates at the lower temperature.

In summary, the combination of the monofilament wire and the noveljoint-making process makes it not only possible, but also practical, tomake a persistent MgB₂ joint. For example, a MM magnet manufacturercould purchase insulated superconducting MgB₂ wire from the wiremanufacturer then simply wind the magnet and make the joint. Therefore,the magnet manufacturer would not be responsible for the performance ofthe wire, in contrast with prior art magnets, where the magnetmanufacturer was responsible for the proper heat treatment of the wirein magnet form and needed to accept the risk of improper heat treatment.Embodiments of the present invention therefore have the potential toreplace some, if not all, of the world's existing MM magnets, given thelooming helium crisis. The technology may open up new markets incountries where that do not even have access to liquid helium.

It will be apparent to those skilled in the art that variousmodifications and variations can be made to the structure of the presentinvention without departing from the scope or spirit of the invention.In view of the foregoing, it is intended that the present inventioncover modifications and variations of this invention provided they fallwithin the scope of the following claims and their equivalents.

What is claimed is:
 1. A method for joining monofilament superconductingwires, comprising the steps of: filling a cavity of a billet with aceramic powder; for each of a first wire and a second wire comprising areacted ceramic monofiliment: shearing an end of the monofilament; andinserting the wire into the billet; inserting a plug configured topartially fill the billet cavity into the billet cavity; and sealing aportion of the billet adjacent to the plug and the wires with a sealingmaterial.
 2. The method of claim 1, further comprising the step ofpressing the plug into the billet to pressurize the ceramic powder. 3.The method of claim 2, wherein the pressing is in a direction alignedwith the first wire and the second wire within the cavity.
 4. The methodof claim 1, wherein the first and second wire each comprises a reactedMgB₂ monofilament.
 5. The method of claim 1, wherein the wire is shearedat an acute angle with respect to a center axis of the wire.
 6. Themethod of claim 1, wherein the ceramic powder comprises Mg+B.
 7. Themethod of claim 1, wherein the billet comprises stainless steel.
 8. Themethod of claim 1, wherein the plug comprises copper.
 9. The method ofclaim 1, further comprising the step of etching a portion of a wirecladding surrounding the end of the monofilament.
 10. The method ofclaim 1, wherein the sealing material comprises a ceramic paste.
 11. Asuperconducting magnet, comprising: a first wire comprising a reactedMgB₂ monofilament; a bobbin; and a coil formed of the first wire woundaround the bobbin.
 12. The superconducting magnet of claim 11, furthercomprising a superconducting wire joint, comprising: a billet comprisinga cavity; a plug configured to partially fill the billet cavity; and thefirst wire and a second wire comprising a reacted MgB₂ monofilament,each of the first and second wire further comprising an end of themonofilament sheared at an acute angle, wherein the first wire end andthe second wire end are disposed within the billet cavity, the firstwire and second wire extending outward from the billet cavity via a gapbetween the billet and the plug, and the billet cavity is filled with apressurized ceramic powder.
 13. The superconducting magnet of claim 11,further comprising a persistent current switch.
 14. The superconductingmagnet of claim 11, wherein the superconducting magnet is configured tooperate above the temperature of liquid helium.
 15. The superconductingmagnet of claim 11, wherein the superconducting magnet is configured tooperate above 10 K.
 16. The superconducting magnet of claim 12, furthercomprising a joint box containing the superconducting wire joint. 17.The superconducting magnet of claim 16, further comprising a furnaceconfigured to maintain superconducting wire joint within the joint boxat a preconfigured temperature.
 18. A method for making asuperconducting magnet, comprising: forming a coil from windings of afirst wire comprising a reacted MgB₂ monofilament; filling a cavity of astainless steel billet with a ceramic powder comprising Mg+B; for eachof the first wire and a second wire comprising a reacted MgB₂monofiliment: shearing an end of the monofilament at an acute angle; andinserting the wire into the billet; inserting a copper plug configuredto partially fill the billet cavity into the billet cavity; and sealinga portion of the billet adjacent to the plug and the wires with aceramic paste.